14 research outputs found
Tuning Magnetic and Structural Transitions through Valence Electron Concentration in the Giant Magnetocaloric Gd<sub>5–<i>x</i></sub>Eu<sub><i>x</i></sub>Ge<sub>4</sub> Phases
Valence electron concentration is a viable chemical tool
to control
the crystal structure and magnetism of Gd<sub>5</sub>Ge<sub>4</sub>. A decrease in the valence electron concentration achieved through
the substitution of Eu<sup>2+</sup> for Gd<sup>3+</sup> leads to the
formation of the interslab Ge–Ge dimers, phase transitions
to the Gd<sub>5</sub>Si<sub>2</sub>Ge<sub>2</sub>- and Gd<sub>5</sub>Si<sub>4</sub>-type structures, and a ferromagnetic ordering in the
Gd<sub>5–<i>x</i></sub>Eu<sub><i>x</i></sub>Ge<sub>4</sub> system. Gd<sub>4.75</sub>Eu<sub>0.25</sub>Ge<sub>4</sub> and Gd<sub>4.50</sub>Eu<sub>0.50</sub>Ge<sub>4</sub> undergo temperature-induced
magnetostructural transformations accompanied by giant magnetocaloric
effects
Electron-Deficient Eu<sub>6.5</sub>Gd<sub>0.5</sub>Ge<sub>6</sub> Intermetallic: A Layered Intergrowth Phase of the Gd<sub>5</sub>Si<sub>4</sub>- and FeB-Type Structures
A novel electron-poor Eu<sub>6.5</sub>Gd<sub>0.5</sub>Ge<sub>6</sub> compound adopts the Ca<sub>7</sub>Sn<sub>6</sub>-type
structure
(space group <i>Pnma</i>, <i>Z</i> = 4, <i>a</i> = 7.5943(5) Å, <i>b</i> = 22.905(1) Å, <i>c</i> = 8.3610(4) Å, and <i>V</i> = 1454.4(1)
Å<sup>3</sup>). The compound can be seen as an intergrowth of
the Gd<sub>5</sub>Si<sub>4</sub>-type (<i>Pnma</i>) R<sub>5</sub>Ge<sub>4</sub> (R = rare earth) and FeB-type (<i>Pnma</i>) RGe compounds. The phase analysis suggests that the Eu<sub>7–<i>x</i></sub>Gd<sub><i>x</i></sub>Ge<sub>6</sub> series
displays a narrow homogneity range of stabilizing the Ca<sub>7</sub>Sn<sub>6</sub> structure at <i>x</i> ≈ 0.5. The
structural results illustrate the structural rigidity of the <sub>∝</sub><sup>2</sup>[R<sub>5</sub>X<sub>4</sub>] slabs (X = <i>p</i>-element) and a possibility
for discovering new intermetallics by combining the <sub>∝</sub><sup>2</sup>[R<sub>5</sub>X<sub>4</sub>] slabs with other symmetry-approximate building blocks. Electronic
structure analysis suggests that the stability and composition of
Eu<sub>6.5</sub>Gd<sub>0.5</sub>Ge<sub>6</sub> represents a compromise
between the valence electron concentration, bonding, and existence
of the neighboring EuGe and (Eu,Gd)<sub>5</sub>Ge<sub>4</sub> phases
Tuning Magnetic and Structural Transitions through Valence Electron Concentration in the Giant Magnetocaloric Gd<sub>5–<i>x</i></sub>Eu<sub><i>x</i></sub>Ge<sub>4</sub> Phases
Valence electron concentration is a viable chemical tool
to control
the crystal structure and magnetism of Gd<sub>5</sub>Ge<sub>4</sub>. A decrease in the valence electron concentration achieved through
the substitution of Eu<sup>2+</sup> for Gd<sup>3+</sup> leads to the
formation of the interslab Ge–Ge dimers, phase transitions
to the Gd<sub>5</sub>Si<sub>2</sub>Ge<sub>2</sub>- and Gd<sub>5</sub>Si<sub>4</sub>-type structures, and a ferromagnetic ordering in the
Gd<sub>5–<i>x</i></sub>Eu<sub><i>x</i></sub>Ge<sub>4</sub> system. Gd<sub>4.75</sub>Eu<sub>0.25</sub>Ge<sub>4</sub> and Gd<sub>4.50</sub>Eu<sub>0.50</sub>Ge<sub>4</sub> undergo temperature-induced
magnetostructural transformations accompanied by giant magnetocaloric
effects
Synthetic Approach for (Mn,Fe)<sub>2</sub>(Si,P) Magnetocaloric Materials: Purity, Structural, Magnetic, and Magnetocaloric Properties
A conventional solid-state
approach has been developed for the synthesis of phase-pure magnetocaloric
Mn<sub>2–<i>x</i></sub>Fe<sub><i>x</i></sub>Si<sub>0.5</sub>P<sub>0.5</sub> materials (<i>x</i> = 0.6,
0.7, 0.8, 0.9). Annealing at high temperatures followed by dwelling
at lower temperatures is essential to obtain pure samples with <i>x</i> = 0.7, 0.8, and 0.9. Structural features of the samples
with <i>x</i> = 0.6 and 0.9 were analyzed as a function
of temperature via synchrotron powder diffraction. The Curie temperature,
temperature hysteresis, and magnetic entropy change were established
from the magnetic measurements. According to the diffraction and magnetization
data, all samples undergo a first-order magnetostructural transition,
but the first-order nature becomes less pronounced for samples that
are more Mn rich
Crystal Cluster Growth and Physical Properties of the EuSbSe<sub>3</sub> and EuBiSe<sub>3</sub> Phases
Syntheses of europium metal, selenium
powder, and the Sb<sub>2</sub>Se<sub>3</sub>/Bi<sub>2</sub>Se<sub>3</sub> binaries were observed to produce crystal clusters of the
EuSbSe<sub>3</sub> and EuBiSe<sub>3</sub> phases. These phases crystallize
with the <i>P</i>2<sub>1</sub>2<sub>1</sub>2<sub>1</sub> space group and can be easily identified based on their growth habits,
forming large clusters of needles. Previous literature suggested that
their structure is charge-balanced with all europium atoms in the
divalent state and one-quarter of the selenium atoms forming trimers.
Physical property measurements on a pure sample of EuSbSe<sub>3</sub> revealed typical Arrhenius-type electrical resistivity, being approximately
3 orders of magnitude too large for thermoelectric applications. Electronic
structure calculations indicated that both EuSbSe<sub>3</sub> and
EuBiSe<sub>3</sub> are narrow-band-gap semiconductors, in good agreement
with the electrical resistivity data. The valence and conduction band
states near the Fermi level are dominated by the Sb/Bi and Se p states,
as expected given their small difference in electronegativity
AlFe<sub>2–<i>x</i></sub>Co<sub><i>x</i></sub>B<sub>2</sub> (<i>x</i> = 0–0.30): <i>T</i><sub>C</sub> Tuning through Co Substitution for a Promising Magnetocaloric Material Realized by Spark Plasma Sintering
AlFe<sub>2</sub>B<sub>2</sub> and
AlFe<sub>2–<i>x</i></sub>Co<sub><i>x</i></sub>B<sub>2</sub> (<i>x</i> = 0–0.30) were synthesized
from the elements in three different ways. The samples were characterized
by powder X-ray diffraction, Rietveld refinements, energy-dispersive
X-ray spectroscopy, and magnetic measurements. Using Al flux the formation
of AlFe<sub>2</sub>B<sub>2</sub> single crystals is preferred. Arc
melting enables the substitution of ∼6% Co. This substitution
of Fe by Co decreases the Curie temperature <i>T</i><sub>C</sub> from 290 to 240 K. The highest Co substitution up to 15%
is achieved by spark plasma sintering (SPS). <i>T</i><sub>C</sub> is reduced to 205 K. In all cases an excess of Al is necessary
to avoid the formation of ferromagnetic FeB. Al<sub>13</sub>Fe<sub>4–<i>x</i></sub>Co<sub><i>x</i></sub> is
the common byproduct. <i>T</i><sub>C</sub> and the cobalt
content are linearly correlated. The transition paramagnetic–ferromagnetic
remains sharp for all examples. The magnetic entropy change of the
Co-containing samples is comparable to AlFe<sub>2</sub>B<sub>2</sub>. SPS synthesis yields, in short reaction times, a homogeneous and
dense material with small amounts of paramagnetic Al<sub>13</sub>Fe<sub>4–x</sub>Co<sub><i>x</i></sub> as an impurity, which
can serve as sinter additive. These properties make AlFe<sub>2–<i>x</i></sub>Co<sub><i>x</i></sub>B<sub>2</sub> a promising
magnetocaloric material for applications between room temperature
and 200 K
Crystal Cluster Growth and Physical Properties of the EuSbSe<sub>3</sub> and EuBiSe<sub>3</sub> Phases
Syntheses of europium metal, selenium
powder, and the Sb<sub>2</sub>Se<sub>3</sub>/Bi<sub>2</sub>Se<sub>3</sub> binaries were observed to produce crystal clusters of the
EuSbSe<sub>3</sub> and EuBiSe<sub>3</sub> phases. These phases crystallize
with the <i>P</i>2<sub>1</sub>2<sub>1</sub>2<sub>1</sub> space group and can be easily identified based on their growth habits,
forming large clusters of needles. Previous literature suggested that
their structure is charge-balanced with all europium atoms in the
divalent state and one-quarter of the selenium atoms forming trimers.
Physical property measurements on a pure sample of EuSbSe<sub>3</sub> revealed typical Arrhenius-type electrical resistivity, being approximately
3 orders of magnitude too large for thermoelectric applications. Electronic
structure calculations indicated that both EuSbSe<sub>3</sub> and
EuBiSe<sub>3</sub> are narrow-band-gap semiconductors, in good agreement
with the electrical resistivity data. The valence and conduction band
states near the Fermi level are dominated by the Sb/Bi and Se p states,
as expected given their small difference in electronegativity
Gd<sub>4</sub>Ge<sub>3–<i>x</i></sub><i>Pn</i><sub><i>x</i></sub> (<i>Pn</i> = P, Sb, Bi, <i>x</i> = 0.5–3): Stabilizing the Nonexisting Gd<sub>4</sub>Ge<sub>3</sub> Binary through Valence Electron Concentration. Electronic and Magnetic Properties of Gd<sub>4</sub>Ge<sub>3–<i>x</i></sub><i>Pn</i><sub><i>x</i></sub>
Gd<sub>4</sub>Ge<sub>3–<i>x</i></sub><i>Pn</i><sub><i>x</i></sub> (<i>Pn</i> = P, Sb, Bi; <i>x</i> = 0.5–3) phases have been
prepared and characterized
using X-ray diffraction, wavelength-dispersive spectroscopy, and magnetization
measurements. All Gd<sub>4</sub>Ge<sub>3–<i>x</i></sub><i>Pn</i><sub><i>x</i></sub> phases adopt
a cubic anti-Th<sub>3</sub>P<sub>4</sub> structure, and no deficiency
on the Gd or <i>p</i>-element site could be detected. Only
one P-containing phase with the Gd<sub>4</sub>Ge<sub>2.51(5)</sub>P<sub>0.49(5)</sub> composition could be obtained, as larger substitution
levels did not yield the phase. Existence of Gd<sub>4</sub>Ge<sub>2.51(5)</sub>P<sub>0.49(5)</sub> and Gd<sub>4</sub>Ge<sub>2.49(3)</sub>Bi<sub>0.51(3)</sub> suggests that the hypothetical Gd<sub>4</sub>Ge<sub>3</sub> binary can be easily stabilized by a small increase
in the valence electron count and that the size of the <i>p</i> element is not a key factor. Electronic structure calculations reveal
that large substitution levels with more electron-rich Sb and Bi are
possible for charge-balanced (Gd<sup>3+</sup>)<sub>4</sub>(Ge<sup>4–</sup>)<sub>3</sub> as extra electrons occupy the bonding
Gd–Gd and Gd–Ge states. This analysis also supports
the stability of Gd<sub>4</sub>Sb<sub>3</sub> and Gd<sub>4</sub>Bi<sub>3</sub>. All Gd<sub>4</sub>Ge<sub>3–<i>x</i></sub><i>Pn</i><sub><i>x</i></sub> phases order ferromagnetically
with relatively high Curie temperatures of 234–356 K. The variation
in the Curie temperatures of the Gd<sub>4</sub>Ge<sub>3–<i>x</i></sub>Sb<sub><i>x</i></sub> and Gd<sub>4</sub>Ge<sub>3–<i>x</i></sub>Bi<sub><i>x</i></sub> series can be explained through the changes in the numbers
of conduction electrons associated with Ge/Sb(Bi) substitution
Disorder-Controlled Electrical Properties in the Ho<sub>2</sub>Sb<sub>1–<i>x</i></sub>Bi<sub><i>x</i></sub>O<sub>2</sub> Systems
High-purity bulk samples of the Ho<sub>2</sub>Sb<sub>1–<i>x</i></sub>Bi<sub><i>x</i></sub>O<sub>2</sub> phases (<i>x</i> =
0, 0.2, 0.4, 0.6, 0.8, 1.0) were prepared
and subjected to structural and elemental analysis as well as physical
property measurements. The Sb/Bi ratio in the Ho<sub>2</sub>Sb<sub>1–<i>x</i></sub>Bi<sub><i>x</i></sub>O<sub>2</sub> system could be fully traversed without disturbing
the overall <i>anti</i>-ThCr<sub>2</sub>Si<sub>2</sub> type structure (<i>I</i>4/<i>mmm</i>). The single-crystal
X-ray diffraction studies revealed that the local atomic displacement
on the Sb/Bi site is reduced with the increasing Bi content. Such
local structural perturbations lead to a gradual semiconductor-to-metal
transition in the bulk materials. The significant variations in the
electrical properties without a change in the charge carrier concentration
are explained within the frame of the disorder-induced Anderson localization.
These experimental observations demonstrated an alternative strategy
for electrical properties manipulations through the control of the
local atomic disorder
Decoupling the Electrical Conductivity and Seebeck Coefficient in the <i>RE</i><sub>2</sub>SbO<sub>2</sub> Compounds through Local Structural Perturbations
Compromise between the electrical conductivity and Seebeck
coefficient
limits the efficiency of chemical doping in the thermoelectric research.
An alternative strategy, involving the control of a local crystal
structure, is demonstrated to improve the thermoelectric performance
in the <i>RE</i><sub>2</sub>SbO<sub>2</sub> system. The <i>RE</i><sub>2</sub>SbO<sub>2</sub> phases, adopting a disordered <i>anti</i>-ThCr<sub>2</sub>Si<sub>2</sub>-type structure (<i>I</i>4/<i>mmm</i>), were prepared for <i>RE</i> = La, Nd, Sm, Gd, Ho, and Er. By traversing the rare earth series,
the lattice parameters of the <i>RE</i><sub>2</sub>SbO<sub>2</sub> phases are gradually reduced, thus increasing chemical pressure
on the Sb environment. As the Sb displacements are perturbed, different
charge carrier activation mechanisms dominate the transport properties
of these compounds. As a result, the electrical conductivity and Seebeck
coefficient are improved simultaneously, while the number of charge
carriers in the series remains constant